EP3397663A1 - Composition polymère transparente et résistante aux chocs et article fabriqué - Google Patents

Composition polymère transparente et résistante aux chocs et article fabriqué

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Publication number
EP3397663A1
EP3397663A1 EP16882468.8A EP16882468A EP3397663A1 EP 3397663 A1 EP3397663 A1 EP 3397663A1 EP 16882468 A EP16882468 A EP 16882468A EP 3397663 A1 EP3397663 A1 EP 3397663A1
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EP
European Patent Office
Prior art keywords
polymer composition
matrix
phase
polymer
dispersed phase
Prior art date
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Granted
Application number
EP16882468.8A
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German (de)
English (en)
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EP3397663B1 (fr
EP3397663A4 (fr
Inventor
Leslie BOCKMAN
Elliot CARNEVALE
Jon Scott LARSON
Kevin HERRINGTON
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Braskem America Inc
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Braskem America Inc
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/10—Homopolymers or copolymers of propene
    • C08L23/12—Polypropene
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C49/00—Blow-moulding, i.e. blowing a preform or parison to a desired shape within a mould; Apparatus therefor
    • B29C49/0005—Blow-moulding, i.e. blowing a preform or parison to a desired shape within a mould; Apparatus therefor characterised by the material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C51/00—Shaping by thermoforming, i.e. shaping sheets or sheet like preforms after heating, e.g. shaping sheets in matched moulds or by deep-drawing; Apparatus therefor
    • B29C51/002—Shaping by thermoforming, i.e. shaping sheets or sheet like preforms after heating, e.g. shaping sheets in matched moulds or by deep-drawing; Apparatus therefor characterised by the choice of material
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/16—Elastomeric ethene-propene or ethene-propene-diene copolymers, e.g. EPR and EPDM rubbers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/18—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms
    • C08L23/20—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms having four to nine carbon atoms
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/18—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms
    • C08L23/24—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms having ten or more carbon atoms
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2023/00—Use of polyalkenes or derivatives thereof as moulding material
    • B29K2023/10—Polymers of propylene
    • B29K2023/12—PP, i.e. polypropylene
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2995/00—Properties of moulding materials, reinforcements, fillers, preformed parts or moulds
    • B29K2995/0018—Properties of moulding materials, reinforcements, fillers, preformed parts or moulds having particular optical properties, e.g. fluorescent or phosphorescent
    • B29K2995/0026—Transparent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2995/00—Properties of moulding materials, reinforcements, fillers, preformed parts or moulds
    • B29K2995/0018—Properties of moulding materials, reinforcements, fillers, preformed parts or moulds having particular optical properties, e.g. fluorescent or phosphorescent
    • B29K2995/0029—Translucent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2995/00—Properties of moulding materials, reinforcements, fillers, preformed parts or moulds
    • B29K2995/0037—Other properties
    • B29K2995/0089—Impact strength or toughness
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2203/00—Applications
    • C08L2203/30—Applications used for thermoforming
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2205/00—Polymer mixtures characterised by other features
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2205/00—Polymer mixtures characterised by other features
    • C08L2205/02—Polymer mixtures characterised by other features containing two or more polymers of the same C08L -group
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2205/00—Polymer mixtures characterised by other features
    • C08L2205/03—Polymer mixtures characterised by other features containing three or more polymers in a blend
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2207/00—Properties characterising the ingredient of the composition
    • C08L2207/02—Heterophasic composition
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2666/00—Composition of polymers characterized by a further compound in the blend, being organic macromolecular compounds, natural resins, waxes or and bituminous materials, non-macromolecular organic substances, inorganic substances or characterized by their function in the composition
    • C08L2666/02—Organic macromolecular compounds, natural resins, waxes or and bituminous materials
    • C08L2666/04—Macromolecular compounds according to groups C08L7/00 - C08L49/00, or C08L55/00 - C08L57/00; Derivatives thereof
    • C08L2666/06—Homopolymers or copolymers of unsaturated hydrocarbons; Derivatives thereof

Definitions

  • the disclosure relates to polymers generally. More particularly, the disclosed subject matter relates to a polymer composition and a fabricated article comprising a
  • polypropylene (PP) copolymer and the method of making the composition and the article.
  • Polypropylene compositions have gained wide commercial acceptance and usage in numerous applications because of the relatively low cost of the polymers and the desirable properties they exhibit.
  • polypropylene polymers particularly propylene
  • ICPs have been able to achieve clarity by refractive index matching the dispersed phase to the matrix material.
  • Other ICPs have sought to achieve clarity by increasing dispersed phase miscibility to achieve particles which are not large enough to affect the light transmission.
  • Known ICPs generally do not provide a combination of good properties including stiffness, toughness and optical transparency.
  • the present invention provides a polymer composition, a fabricated article comprising such a composition, and methods of making the same.
  • a polymer composition comprises from about 40 weight percent (wt.%) to about 99.9 wt.% (e.g., 50-95 wt.% or 75- 92%) of a continuous matrix phase; and from about 0.01 wt.% to about 60 wt.% (e.g., 5-50 wt.%)) of a dispersed phase.
  • the weight percentages of the matrix phase and the dispersed phase are based on the total weight of the matrix phase and the dispersed phase.
  • the matrix phase may comprise a polypropylene polymer comprising from 0 to 7 mole percent (mol.%>) (e.g., 0.01-4 mol.%)) of units derived from ethylene, a C4-C10 alpha olefin or combinations thereof.
  • the dispersed phases may be a propylene/alpha olefin copolymer having from 10 mol.%> to 70 mol.%> (e.g., from 35 mol.%> to 60 mol.%>) of units derived from ethylene or a C4-C10 alpha olefin or combinations thereof.
  • the polymer composition satisfies the following inequality:
  • x is a ratio of Mw solubles/Mw insolubles and is less than or equal to 0.85
  • Mw solubles is weight average molecular weight of a soluble fraction of the polymer composition in xylene at 25°C following ASTM D5492
  • Mw insoluble is weight average molecular weight of an insoluble fraction of the polymer composition in xylene at 25°C following ASTM D5492
  • y is the haze value being measured on an injection molded plaque having a thickness of 0.508 millimeter (20 mil) according to ASTM D1003.
  • the dispersed phase has an intrinsic viscosity from about
  • the matrix phase has a melt flow rate (MFR) from about 0.1 dg/min. to about 10 dg/min. (for example, from about 0.1 dg/min. to about 2 dg/min.).
  • the dispersed phase has a melt flow rate (MFR) of from about 10 dg/min. to about 200 dg/min. (for example, from about 20 dg/min. to about 60 dg/min.).
  • the melt flow rates in this disclosure are measured using a load of 2.16 kg at 230 °C following ASTM D 1238.
  • the matrix phase may comprise from about 0.01 mol. %> to about 5 mol.%> of ethylene in some embodiments.
  • the polymer composition comprising the matrix phase and the dispersed phase is made through an in-reactor process.
  • the monomers are feed into one or more reactors for polymerization, and a resulting polymer composition having the two-phase structure described herein is obtained.
  • the polymer composition comprising the matrix phase and the dispersed phase is made through a post-reactor process by blending a first polymer ingredient and a second polymer ingredient.
  • the first polymer ingredient mainly contributes to the matrix phase while the second polymer ingredient mainly contributes to the dispersed phase.
  • the first polymer ingredient may be a propylene-based homopolymer or a random copolymer.
  • the second polymer ingredient may be an impact copolymer (ICP).
  • ICP impact copolymer
  • the matrix phase of the resulting polymer composition as described herein includes the first polymer ingredient and the matrix portion of the second polymer ingredient.
  • the matrix phase is a combined matrix phase.
  • the polymer composition may further comprise a clarifying agent.
  • the clarifying agent may be present at a final concentration equal to or less than 8,000 ppm (e.g., 1- 8,000 ppm).
  • the dispersed phase in the matrix phase may have a phase domain size smaller than 700 nm (e.g., from 0.1 nm to 700 nm).
  • the polymer composition may have a melt flow rate of from about 0.5 dg/min. (or 1 dg/min.) to about 10 dg/min. (measured using a load of 2.16 kg at 230 °C following ASTM D 1238).
  • the composition can be made through blending /compounding the ingredients.
  • the polymer composition may have a ratio of ⁇ / ⁇ less than 1.2 according to the formula:
  • MFRi is the melt flow of the matrix phase (or the combined matrix phase) only and MFR2 is the overall melt flow of the polymer composition.
  • the polymer composition may also have a polydispersity index (PDI, i.e. the ratio of Mw/Mn) greater than 4.
  • PDI polydispersity index
  • Mw and Mn are weight average molecular weight and number average molecular weight, respectively.
  • the resulting polymer composition provides a combination of excellent optical transparency, toughness, impact resistance and rigidity.
  • the polymer composition after being molded has a haze value less than 30%, which is measured using at an injection molded plaque having a thickness of 0.508 millimeter (20 mil) following ASTM D1003.
  • the composition may have a flexural modulus greater than 1000 MPa (measured at 23 °C according to ASTM D 790), and a notched Izod impact strength greater than 1.4 ft-lbs/in, for example, 5 ft-lbs/in. (measured at 23 °C according to ASTM D 256).
  • the composition may have a heat deflection temperature greater than 75°C at 0.46 MPa (66 psi) according to ASTM D648.
  • the present disclosure provides a fabricated article comprising the polymer composition described above, and a method for making the fabricated article.
  • a fabricated article might be manufactured by a blow molding or thermoforming process.
  • the material in the fabricated article has the structure and the properties as described above.
  • the article has a haze value less than 30% and a top load value greater than 20 1b-ft.
  • FIG. 1 illustrates the effect of the melt flow of the polymer composition on its haze in accordance with some embodiments.
  • FIG. 2 illustrates haze of polypropylene based composition as a function of comonomer (e.g., ethylene) content in the matrix in some embodiments.
  • comonomer e.g., ethylene
  • FIG. 3 illustrates haze of polypropylene based composition as a function of loading percentage of a clarifying agent in some embodiments.
  • FIGS. 4A-4D show atomic force microscopy (AFM) images of the experimental samples (lOOOx magnification, 14.5 ⁇ across in each image).
  • FIG. 5 is a transmission electronic microscopy (TEM) image of the experimental sample (Ex. 20) (2 ⁇ of legend mark and 10.52 x 15. 2 ⁇ for field of view in size).
  • TEM transmission electronic microscopy
  • FIGS. 6A-6B illustrate haze of the polymer composition as a function of Mw solubles /Mw Insolubles in some embodiments.
  • Random copolymers i.e., single phase polypropylene with a comonomer, have been used for applications that require clarity. These random copolymers, however, tend to be soft, and have low heat distortion temperatures. Thee random copolymers do not have desirable physical properties for applications where impact copolymers are normally used, particularly impact resistance at cold temperatures (e.g., about 4 °C). These materials exhibit brittle behavior around 0°C.
  • rubbers such as metallocene copolymers (elastomers and plastomers) and styrenic block copolymers are sometimes blended into polypropylene.
  • These additives work by either (a) having refractive indices that match that of polypropylene (approximately 1.50 micron) or (b) particle sizes that are small enough not to refract light and therefore cause haze.
  • Incorporation of such additive components into polypropylene is not desirable, for a number of reasons.
  • the metallocene elastomers and styrenic block copolymers are often costly to produce relative to conventional Ziegler-Natta polypropylene (ZN-PP).
  • ZN-PP Ziegler-Natta polypropylene
  • multiphase propylene copolymers having good impact toughness and decreasing stiffness can be prepared by means of Ziegler-Natta catalyst systems in a multistage polymerization reaction.
  • the compositions that incorporate ethylene-propylene copolymers having a high proportion of ethylene into a polymer matrix make the multiphase propylene copolymer turbid. Poor miscibility of the dispersed phase with the polymer matrix leads to a separation of the phases and thus to turbidity and to poor transparency values of the heterogeneous copolymer.
  • a low melt flow impact copolymer can be blended into a low melt homopolymer in order to achieve ductile behavior for applications that require toughness (such as containers intended for refrigerator and/or freezer conditions). While these materials may be quite ductile, they are completely opaque and offer no see-through properties.
  • an elastomer may be blended into a random copolymer to offer additional toughness.
  • These elastomers provide toughness while still offering good optical properties by either matching the refractive index of PP or by being completely miscible in PP.
  • these elastomers are limited in loading addition due to stickiness during processing and they typically add softness (lower stiffness and heat distortion) to the parts.
  • propylene ICPs are also made in-reactor using Ziegler-Natta catalysts. The resulting propylene ICPs have heterophasic copolymer structure and provide high clarity, low haze and high toughness.
  • the inventors have invented a new approach to address this market need for stiff, tough and clear propylene based polymers by having a polymer composition having a matrix phase and a dispersed phase as described herein.
  • the polymer composition can be made through an in-reactor process or a post-reactor blending process.
  • the polymer composition is achieved by combining a high melt flow (low molecular weight) copolymer as a dispersed phase with a very low melt flow (high molecular weight) homopolymer or copolymer as a matrix phase.
  • Both the matrix phase and the dispersed phase are propylene-based and have specific structures as described herein.
  • the resulting polymer composition and the fabricated article have excellent clarity, strength, toughness but low haze.
  • the resulting material offers toughness of an impact copolymer and optical properties that are similar to a random copolymer.
  • the dispersed phase such as an impact copolymer (ICP) is dispersed in a homopolymer matrix
  • the resulting composition offers much better impact resistance than a typical impact modified homopolymer and significantly higher stiffness and a higher heat distortion
  • a dispersed phase such as an ICP having a high melt flow is dispersed in a random copolymer matrix having a low melt flow, particularly when the melt flow of the ICP is higher than that of the random copolymer, the resulting composition provides improved clarity (i.e. low haze), with a good balance of mechanical properties such as impact resistance.
  • the present invention provides a polymer composition, a fabricated article comprising such a composition, and methods of making the same.
  • polymer refers to a polymeric compound prepared by polymerizing monomers, whether of the same or a different type.
  • homopolymer refers to a polymer prepared from only one type of monomer, and the term “copolymer” refers to a polymer derived from two or more different monomers.
  • Polypropylene or "a propylene based polymer” refers to a polymer comprising greater than 50% by weight of units which have been derived from propylene monomer. This includes polypropylene homopolymers (derived from close to or equal to 100% of propylene), or copolymers (comprising units derived from two or more comonomers).
  • a propylene impact copolymer has a two-phase structure, comprising: (a) a matrix (or main segment) comprising a polypropylene homopolymer or a propylene/alpha-olefin random copolymer which comprises greater than 50 wt. % of units derived from propylene monomer, and (b) a dispersed phase (or dispersion segment) comprising a copolymer of ethylene and a C3-C8 a-olefin (e.g., an ethylene-propylene copolymer).
  • Density is determined in accordance with ASTM D792.
  • melt flow rate MFR
  • melt index units of g/10 min or dg/min.
  • F c refers to the percent by weight of the dispersed phase in the total polymer composition. In general F c is equal to the ratio of amount of dispersed rubber phase to the total amount of material made. F c can be measured by the weight percent of the total xylene solubles, i.e. that of the matrix, in the polymer composition.
  • Mf of the dispersed phase can be calculated following a general equation:
  • MFf xa In (MFa) + xb In (MFb), where xa is weight fraction of component A, xb is weight fraction of component B, xa + xb is equal to 1, Mfa is melt flow index of component A, MFb is melt flow index of component B, and MFf is the final melt flow of the composition having A and B.
  • xa and xb can be measured from the data of xylene solubles and insoluble. Melt flow of the matrix and the final composition can be measured.
  • Beta/alpha ( ⁇ / ⁇ ) is conceptually the ratio of the molecular weight of the dispersed phase to the molecular weight of the matrix phaset. On a practical level, ⁇ / ⁇ is defined according to the following equation:
  • MFRi is the melt flow of matrix (or the combined matrix phase) only and MFR 2 is the overall melt flow of the polymer composition.
  • AFM atomic force microscopy
  • TEM transmission electron microscopy
  • haze generally refers to an appearance cause by scattered light upon passing through a film or sheet of a material can produce a smoky or translucent field.
  • the haze of the present invention is measured using ASTM D1003-97.
  • clarity generally refers to the amount of luminous transmittance described according to and measured per ASTM D1003.
  • flexural modulus (expressed in units of PSI) is the one percent secant modulus, which is further described according to and measured per ASTM D790 at 230°C.
  • notched Izod impact strength (expressed in ft-lbs/in) was measured at 23 °C as described according to and measured per ASTM D256.
  • Ceast impact was measured at 0, 4, and 23 °C according to ASTM D3763 - 10 in the GC configuration. It is expressed in in-lbs. This impact test is a multiaxial impact test, and may provide a more representative result for impact resistance for many applications.
  • DSC differential scanning calorimetry
  • a sheet of a polymer is placed into a light aluminum pan (about 50 mg) and crimped shut.
  • a DSC scan of the polymer sample is performed in the temperature range of -20 °C to 200 °C using a rate of 10 °C/min. Melting points of crystalline phases in a polymer composition can be determined using DSC.
  • a ratio of Mw solubles/Mw insolubles refers as a viscosity ratio.
  • Mw solubles is weight average molecular weight of a soluble fraction of the polymer composition in xylene at 25°C following ASTM D5492
  • Mw insolubles is weight average molecular weight of an insoluble fraction of the polymer composition in xylene at 25°C following ASTM D5492.
  • the molecular weight values of the soluble fraction and the insoluble fraction were measured using gel permeation chromatography (GPC).
  • a "top load value” refers to a crush load strength, which is the amount of force of load a cup can withstand before showing signs of buckling or cracking, following a testing method developed by the applicant.
  • the samples are injection molded cups.
  • the object of the test is to determine the crush load properties of injection molded cups to understand the fundamental stiffness and yield load characteristics of the material before buckling under a uniform compression load tester.
  • the crush properties test is subjected to compression loads to determine the relative crush resistance of molded cups.
  • the test uses the MTS Sintech 6 universal tester system with Test Works 3.0 software to study the load-deflection characteristics of the molded cup under parallel plate loading. The cup sits between two parallel plates- one of which is stationary.
  • a constant speed of 0.254 centimeter /minute (0.1 inches/min) is used.
  • a load cell measures the applied force. The test is commenced by lowering the movable crosshead at a speed of 0.254 centimeter/minute (0.1 in/min) over the specimen. A maximum load is applied until failure via buckling of the tested cup is observed.
  • the polymer composition comprises from about 40 wt.% to about 99.9 wt.% (e.g., from about 50 wt. % to about 95 wt.%, or from about 75 wt. % to about 92 wt.%) of a matrix phase; and from about 0.01 wt.% to about 60 wt.% (e.g., from about 5 wt.% to about 50 wt.%, or from about 8 wt.% to about 25 wt.%) of a dispersed phase.
  • the matrix phase is continuous.
  • the weight percentages of the matrix phase and the dispersed phase are based on the total weight of the matrix phase and the dispersed phase.
  • the matrix phase may comprise a polypropylene polymer comprising from 0 to 7 mol.% (e.g., from 0.01 mol.% to 4 mol.%) of units derived from ethylene, a C4-C10 alpha olefin or combinations thereof.
  • the dispersed phase may be a propylene/alpha olefin copolymer having from 10 mol.% to 70 mol.% (e.g., from 35 mol.% to 60 mol.%) of units derived from ethylene or a C4-C10 alpha olefin or combinations thereof.
  • the weight percentage of the comonomer of ethylene or a C4-C10 alpha olefin may be in the range from 7 wt.% to 50 wt.% (e.g., from 25 wt.% to 40 wt.%).
  • alpha-olefin as comonomer include but are not limited to butene, pentene, hexene, or octene.
  • the dispersed phase is a propylene/alpha olefin copolymer having from 40 mol.% to 57 mol.% of units derived from ethylene or a C4-C10 alpha olefin or combinations thereof.
  • the polymer composition satisfies the following inequality in some embodiments:
  • x is a ratio of Mw solubles/Mw insolubles and is less than or equal to 0.85
  • Mw solubles is weight average molecular weight of a soluble fraction of the polymer composition in xylene at 25°C following ASTM D5492
  • Mw insoluble is weight average molecular weight of an insoluble fraction of the polymer composition in xylene at 25°C following ASTM D5492
  • y is the haze value being measured on a sheet with a thickness of 0.508 millimeter (20 mil) according to ASTM D1003.
  • the propylene polymer of the matrix phase polymer may comprise from 0.01 molar percent (mol. %) to 5 mol.% of ethylene in some embodiments.
  • the matrix phase has a melt flow rate (MFR) of from about
  • the dispersed phase has a melt flow rate (MFR) of from about 1 dg/min. to about 200 dg/min. (for example, from about 10 dg/min. to about 200 dg/min., or from about 20 dg/min. to about 60 dg/min.).
  • MFR melt flow rate
  • the MFT of the dispersed phase is in one of the following ranges: 1-100; 1-50, 1-25 and 1-15.
  • the dispersed phase may have an intrinsic viscosity of from about 0.5 to about 3 (e.g., from about 1 to about 2).
  • the polymer composition comprising the matrix phase and the dispersed phase is made through an in-reactor process.
  • the monomers are feed into a reactor for polymerization, and a resulting polymer composition having the two-phase structure described herein is obtained.
  • the polymer composition comprising the matrix phase and the dispersed phase is made through a post-reactor process by blending a first polymer ingredient and a second polymer ingredient.
  • the first polymer ingredient mainly contributes to the matrix phase while the second polymer ingredient mainly contributes to the dispersed phase.
  • the first polymer ingredient may be a propylene-based homopolymer or a random copolymer.
  • the second polymer ingredient may be an impact copolymer (ICP).
  • ICP impact copolymer
  • the matrix phase of the resulting polymer composition as described herein includes the first polymer ingredient and the matrix portion of the second polymer ingredient.
  • the matrix phase is a combined matrix phase.
  • the first and the second polymer ingredients may have the percentages and the properties of the matrix phase and the dispersed phase as described herein.
  • the first polymer ingredient may be in the range of from about 40 wt.% to about 99.9 wt.% (e.g., from about 50 wt. % to about 95 wt.%).
  • the second polymer ingredient may also be in the range of from about 0.01 wt.% to about 60 wt.% (e.g., from about 5 wt.% to about 50 wt.% ) based on the total weight of the first and the second polymer ingredients.
  • a random copolymer may comprise from 0.01 molar percent (mol. %) to 5 mol.% of ethylene in some embodiments.
  • the ICP may be a heterophasic (e.g, two-phase) copolymer comprising: (a) a main segment comprising a polypropylene homopolymer or a propylene/alpha-olefin random copolymer which comprises greater than 50 wt. % of units derived from propylene monomer, and (b) a dispersion segment having a copolymer derived from ethylene, a C3-C8 a-olefin, or any combination thereof.
  • the ICP has a crystalline structure having at least one (e.g., one or two) melting point, for example, between 100 °C and 130 °C, in some embodiments.
  • two melting points are present in a two-phase ICP.
  • An exemplary ICP comprises ethylene and propylene, and the content of ethylene is from about 1 wt.% to 50 wt.% of the total weight of the ICP.
  • the ICP may be made using Ziegler-Natta catalyst in an in-reactor solution.
  • the propylene ICP may have a two-phase structure comprising: (a) a main segment comprising a polypropylene homopolymer or a propylene/alpha-olefin random copolymer which comprises greater than 50 wt.
  • a dispersion segment comprising a copolymer of ethylene and a C3-C8 ⁇ -olefin (e.g., an ethylene-propylene copolymer).
  • a suitable alpha-olefin as comonomer include but are not limited to butene, pentene, hexene, or octene.
  • the main segment is a propylene/alpha olefin random copolymer optionally comprising from 0.01 wt.% to 5 wt. %, for example, less than about 2.0 wt.%, of ethylene.
  • the dispersion segment can be in the range from 5 wt.% to 20 wt.% of the total weight of the ICP.
  • the ICP has a first melting point being greater than 100 °C and a second melting point.
  • both the first melting point and the second melting point are greater than 100 °C.
  • An ICP can have a first melting point in the range of from 100 °C to 130 °C (e.g., 120 °C). The first melting point may be attributed to that of the dispersed phase in some embodiments.
  • the second melting point may be in the range from 100 °C to 180 °C (e.g., 150 °C, 165 °C or any other suitable temperature). The second melting point may be attributed to that of the matrix phase in some embodiments.
  • the ICP can be made using one or more matrix phase polymerization steps, occurring in one or more gas phase reactors; one or more dispersed phase polymerization steps, occurring in one or more liquid phase reactors; and at least one de-gassing step.
  • the propylene ICP is made in an in-reactor comprising monomer including propylene and a comonomer such as ethylene. The polymerization is catalyzed with Ziegler- Natta catalyst.
  • a propylene ICP made of propylene and ethylene and consisting essentially of propylene and ethylene moieties are preferred in some embodiments.
  • Catalysts employed in the polymerization of a-olefins may be characterized as supported catalysts or unsupported catalysts, sometimes referred to as homogeneous catalysts.
  • the so-called conventional Ziegler-Natta catalysts are stereospecific complexes formed from a transition metal halide and a metal alkyl or hydride, such as titanium tetrachloride supported on an active magnesium dichloride.
  • a supported catalyst component includes, but is not necessarily limited to, titanium tetrachloride supported on an "active" anhydrous magnesium dihalide, such as magnesium dichloride or magnesium dibromide.
  • a supported catalyst component may be employed in conjunction with a co-catalyst such as an alkylaluminum compound, for example, triethylaluminum (TEAL).
  • a co-catalyst such as an alkylaluminum compound, for example, triethylaluminum (TEAL).
  • TEAL triethylaluminum
  • the Ziegler-Natta catalysts may also incorporate an electron donor compound that may take the form of various amines, phosphenes, esters, aldehydes, and alcohols.
  • the propylene ICP may include a matrix and a dispersed phase.
  • the matrix comprises a polypropylene homopolymer or a propylene/alpha-olefin random copolymer which comprises greater than 50 wt. % of units derived from propylene monomer.
  • the matrix is a propylene/alpha olefin random copolymer optionally comprising from 0.01 wt.% to 5 wt. %, for example, less than about 2.0 wt.%, of ethylene.
  • the dispersed phase comprises a copolymer of ethylene and a C3-C8 a-olefin (e.g., an ethylene-propylene copolymer). In some embodiments, the dispersed phase can be in the range from 5 wt.% to 20 wt.% of the total weight of the ICP.
  • the propylene ICP may be a copolymer comprising propylene and ethylene moieties and having two phase structures. When such an ICP is added as a second polymer ingredient, the matrix of the final polymer composition includes the combined matrix from the first and the second polymer ingredient. In some embodiments, the combined matrix includes the first polymer ingredient and the matrix portion of the ICP.
  • the polymer composition may further comprise a clarifying agent.
  • the clarifying agent may be present at a final concentration equal to or less than 8,000 ppm (e.g., 1- 8,000 ppm, or 5 ppm- 5,000 ppm).
  • the final concentration of the clarifying agent may include the clarifying agent in the first and/or second polymer ingredients, and the additional clarifying agents added during the step of preparing the final polymer composition.
  • suitable clarifying agents include but are not limited to dibenzylidene sorbitol acetal derivatives such as l,3-o-2,4- bis(3,4-dimethylbenzylidene)sorbitol (available from Milliken Chemical Company, Spartanburg, S.C., known as MILLAD® 3988), l,3-o-2,4-bis(p-methylbenzylidene)sorbitol (available from Milliken Chemical and known as MILLAD® 3940), sodium 2,2'-methylene-bis-(4,6-di-tert- butylphenyl) phosphate (from Asahi Denka Kogyo K.
  • dibenzylidene sorbitol acetal derivatives such as l,3-o-2,4- bis(3,4-dimethylbenzylidene)sorbitol (available from Milliken Chemical Company, Spartanburg, S.C., known as MILLAD® 3988), l,3-o-2,
  • NA-11 aluminum bis[2,2'- methylene-bis-(4,6-di-tert-butylphenyl)phosphate] with lithium myristate (also from Asahi Denka Kogyo K. K., known as NA-21), other suitable nucleators and combinations thereof.
  • a clarifying agent that is soluble in polypropylene e.g., MILLAD NX8000, available from Milliken
  • MILLAD NX8000 available from Milliken
  • the dispersed phase in the continuous matrix may have a phase domain size smaller than 700 nm (e.g., from 0.1 nm to 700 nm).
  • the polymer composition may have a melt flow rate of from about 0.5 dg/min. to about 10 dg/min, for example, from about 1 dg/min. to about 10 dg/min. (measured using a load of 2.16 kg at 230 °C following ASTM D 1238).
  • the MFR of the polymer composition is one of the following ranges: 0.5-8, 0.5-6 and 0.5-4.
  • the composition can be made through blending /compounding the ingredients.
  • the polymer ingredients may be combined by way of dry blending and/or melt blending.
  • a single screw or twin screw extruder, or other suitable compounding equipment can be used.
  • the invention aims to offer a solution that provides a unique set of properties
  • the dispersed phase or particles can be forced to elongate below the wavelength of light when during processing where there is either shear forces, such as injection molding of 0.508 millimeter (20 mil) thick disks, or through orientation that is imparted during the processes (such as thermoforming or blow molding). Previously it was believed that this response would only work in high shear environments typical of injection molding.
  • high molecular weight materials (low MF ⁇ 3 dg/min.) are not injection molded but are converted via processes such as thermoforming or blow molding or even cast film, where the shear is low but they are elongational forces on the materials.
  • the viscosity of a dispersed phase is lower than that of the matrix, the dispersed particles will elongate below the wavelength of light in high shear processes or low shear processes where some orientation is imparted.
  • the polymer composition may have a ratio of ⁇ / ⁇ less than 1.2 according to the formula:
  • MFRi is the melt flow of the matrix (or combined matrix) phase only and MFR2 is the overall melt flow of the polymer composition.
  • MFR2 is the overall melt flow of the polymer composition.
  • the calculation of the ratio of ⁇ / ⁇ is further illustrated with the examples below.
  • the polymer composition may also have a Mw/Mn greater than 4.
  • the resulting polymer composition provides a combination of excellent optical transparency, toughness, impact resistance and rigidity.
  • the polymer composition after being molded has a haze value less than 30% (e.g., less than 28% or 25%, or 0.01%-20%), which is measured using at an injection molded plaque having a thickness of 0.508 millimeter (20 mil) following ASTM D1003.
  • the composition may have a flexural modulus equal to or greater than 1,000 MPa (e.g., 1,000 MPa -3,000 MPa, measured at 23 °C according to ASTM D 790), and a notched Izod impact strength equal to or greater than 1.4 ft-lbs/in (e.g., 1.4 ft-lbs/in - 5.0 ft-lbs/in, measured at 23 °C according to ASTM D 256).
  • the composition may have a heat deflection temperature equal to or greater than 75°C (e.g., 75°C -150°C, at 0.46 MPa (66 psi) according to ASTM D648.
  • Polymer Al is a reactor grade homopolymer (HOMO) of propylene, available from Braskem. Polymer Al has a melt flow index of 0.8 dg/min. and a total xylene solubles of 2.5 wt.%. Polymer Al has high melt strength and excellent rigidity.
  • HOMO reactor grade homopolymer
  • Polymer A2 is a random copolymer (RACO) of propylene and about 2.7 wt.% of ethylene, available from Braskem. Polymer A2 has a melt flow of 2 dg/min. and an overall xylene solubles of 5.8 wt.%.
  • RACO random copolymer
  • Polymer A3 is a reactor grade homopolymer (HOMO) of propylene, available from Braskem. Polymer A3 has a melt flow index of 2.0 dg/min. and a total xylene solubles of 4 wt.%.
  • Polymer A4 is a reactor grade homopolymer (HOMO) of propylene, available from Braskem. Polymer A4 has a melt flow index of about 1.3 dg/min. and a total xylene solubles of 4 wt.%.
  • Polymer A5 is a reactor grade homopolymer (HOMO) of propylene, available from Braskem. Polymer A5 has a melt flow index of about 3.4 dg/min. and a total xylene solubles of 1.7 wt.%.
  • HOMO reactor grade homopolymer
  • Polymer A6 is a reactor grade homopolymer (HOMO) of propylene, available from Braskem. Polymer A6 has a melt flow index of about 12 dg/min. and a total xylene solubles of 3 wt.%.
  • HOMO reactor grade homopolymer
  • Polymer A7 is a reactor grade homopolymer (HOMO) of propylene having high crystalline and MF of 35 dg/min, available from Braskem. Polymer A7 has a total xylene soluble content of 1.2 wt. %.
  • HOMO reactor grade homopolymer
  • Polymer Bl is a heterophasic propylene ICP, available from Braskem.
  • the matrix phase is a homopolymer of propylene with 2 wt. % of an overall xylene solubles content in the matrix.
  • the dispersed phase is 30 wt.% of the total weight of Polymer B l, with an overall ethylene content in the final polymer of 15.6 wt. %.
  • Polymer Bl has melting point of 163 °C(measured using DSC at a rate of 10 °C/min).
  • the blends with Bl are typically nucleated with 4000 ppmJVIilliken® NX®8000, available from Milliken Chemical Company; however, other nucleating agents and clarifying agents were also studied.
  • Polymer B2 is a heterophasic propylene ICP, available from Braskem.
  • the matrix phase is homopolymer of propylene with 1.6 wt. % of an overall xylene solubles content in the matrix.
  • the dispersed phase is 12 wt.% of the total weight of Polymer B2, and has a total overall ethylene content of 10 wt. %.
  • Polymer B2 has melting point of 165°C (measured using DSC at a rate of 10 °C/min).
  • the pellets are generally nucleated with ppm micronized sodium benzoate in order to increase crystallization temperature and flexural modulus. A higher performing nucleating agent and/or clarifying agent is not used as this product is not expected to produce transparent parts.
  • Milliken® NX®8000 available from Milliken Chemical Company, is a clarifying agent that is soluble in polypropylene.
  • Example 1-7 The first two examples (Ex. 1 and Ex. 2) are two preferred examples in some embodiments.
  • Examples 3-6 show that when both the ICP (i.e. the dispersion phase) and the random copolymer or the homopolymer (i.e. the matrix) have the same melt index (e.g., 2 dg/min.), impact resistance is improved compared to the matrix itself. However, the haze is high.
  • Example 7 shows that the improvement in haze can be also achieved without using a clarifying agent in some embodiments.
  • Polymer Al has a haze of 25.4% and non-nucleated Polymer Bl has a haze of 88 % (both on 0.508 millimeter (20 mil) injection molded plaques).
  • the polymer composition may have a ratio of ⁇ / ⁇ less than 1.2 according to the formula:
  • MFRi is the melt flow of the combined matrix phase only
  • MFR2 is the overall melt flow of the polymer composition
  • F c refers to the percent by weight of the dispersed rubber 0 (or called bipolymer) phase in the total polymer composition.
  • Fc refers to the weight percentage of all the pure "rubber" phase of the ICP portion in the total polymer composition.
  • the combined matrix phase includes the matrix of the first polymer ingredient (e.g., homopolymer) and the matrix from the ICP portion. Generally the size of the dispersed phase decreases as the ratio of ⁇ / ⁇ decreases.
  • a pseudo "Rubber MF" are calculated for the ICP component, which comprises a main segment (or ICP matrix) and a dispersion segment (or ICP rubber phase), using the following equation:
  • This ICP having MF of 50 was then blended into a material with a much higher molecular weight (either a homopolymer or a random copolymer), such as a fraction melt flow homopolymer having a melt flow of 0.8 dg/min. To determine the ⁇ / ⁇ of this final blend, several calculations were performed. First, the overall matrix MF of the combination of the low MW ICP and the high MW matrix was determined by the following:
  • Fraction Low MW Matrix is calculated as follows:
  • a 70% blend of a high MF Matrix having a MF of 0.8 dg/min with a 30% blend of a low MW ICP having a final matrix MF of 145 and a fraction bipolymer of 0.30 results in a Combined Matrix Melt Flow of 2.4 dg/min.
  • the rubber phase will have an increased ability to elongate below the wavelength of light as ⁇ / ⁇ decreases. It is more desirable that ⁇ / ⁇ is less than 1. As shown in Table 3, clarity of a 0.508 millimeter (20 mil) thick injection molded disk significantly increases as the ⁇ / ⁇ increases; however, with these combinations, the amount of rubber also increases.
  • haze of polypropylene is generally understood to be a function of comonomer content in the matrix (typically ethylene) and clarifier loading levels, as shown in FIG. 2 and FIG. 3.
  • an impact copolymer even when heavily clarified (e.g., with 4000 ppm NX8000 in Comparative Example CEx. 2) does not yield good optical properties. It is opaque because the rubber particles scatter large amounts of light due to their size and spherical nature. Homopolymers, on the other hand, exhibit good optical properties when they are combined with a large loading of a clarifying agent (CEx. 1), but provide relatively low impact resistance.
  • a clarifying agent CEx. 1
  • Resulting Haze Fraction PP1 *Haze of PPl+Fraction of PP2*Haze of PP2
  • FIGS. 4A-4D show AFM images of the experimental samples at lOOOx magnification. Each image shows a sample size of 14.5 ⁇ across. The dispersed rubber phases have a size of less than 700 nm.
  • the polymer composition can be achieved as a single pellet solution via proper product design, in which a high molecular weight matrix and a lower molecular weight rubber are utilized.
  • a high molecular weight matrix and a lower molecular weight rubber are utilized.
  • One example (Example 16) of such a design is:
  • Example 16 is was made by compounding 70 wt.%> Polymer Al powder and 30%> Polymer Bl powder with the following additives: 1200 ppm AO B215 (antioxidant for MW control)_
  • the compounding was performed on an 18 mm twin screw extruder using an average temperature profile of 210°C, a screw speed of 250 rpm and a feed rate of 6.0 kg/hr.
  • Examples 1-15 above were made by a post-reactor process by blending a first and a second polymer ingredients as described above.
  • Examples 16-21 below were made by an in- reactor process in which the polymer composition was obtained through the in-reactor polymerization process.
  • Examples 17-21 in Table 6 further illustrate the polymer compositions achieved as an in reactor single pellet solution via proper product design, in which a high molecular weight matrix and a lower molecular weight rubber are utilized.
  • Examples 17-21 are ICPs obtained through an in-reactor process, and have a two-phase structure.
  • the matrix phase is a propylene homopolymer with 2 wt.% of the of the overall xylene solubles in the matrix.
  • the amount of the dispersed phase, the molecular weight of the dispersed phase, and the ethylene content in the dispersed phase were varied.
  • Pellets were made by compounding one of the heterophasic propylene ICP with :
  • FIG. 5 shows an exemplary TEM image of the experimental samples such as
  • Example 20 is a sample made through an in-reactor polymerization. The image shows a sample size of 14.5 ⁇ across. The dispersed rubber phases have a size of less than 700 nm.
  • FIGS. 6A-6B illustrate haze of the polymer composition as a function of a viscosity ratio (Mw solubles /Mw Insolubles) in some embodiments.
  • FIG. 6A shows the data for Examples 11-13 and 17-21.
  • FIG. 6B shows the data for Examples 11-21 and B l .
  • the present disclosure provides a fabricated article comprising the polymer composition described above, and a method for making the fabricated article.
  • a fabricated article might be manufactured by a blow molding or thermoforming process.
  • the material in the fabricated article has the structure and the properties as described above.
  • the article has a haze value less than 30%.
  • the article has a top load value greater than 20 lb-ft.

Abstract

La présente invention concerne une composition polymère présentant une transparence optique et une résistance à l'impact comprenant d'environ 40 % en poids (% en pds) à environ 99,9 % en pds (par exemple, de 50 à 95 % en pds) d'une matrice continue, et d'environ 0,01 % en pds à environ 60 % en pds (par exemple, de 5 à 50 % en pds) d'une phase dispersée. Les pourcentages en poids de la phase formant matrice et de la phase dispersée sont basés sur le poids total de la phase formant matrice et de la phase dispersée. La phase formant matrice peut comprendre un polymère de polypropylène comprenant de 0 à 7 % en mole (% en mole) de motifs dérivés d'éthylène, d'alpha oléfine en C4 à C10 ou des combinaisons de ces derniers. Les phases dispersées peuvent être un copolymère de propylène/alpha oléfine ayant de 10 % en mole à 70 % en mole de motifs dérivés d'éthylène ou d'une alpha oléfine en C4 à C10 ou des combinaisons de ces derniers.
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3926005A4 (fr) * 2019-02-12 2023-03-08 Furukawa Electric Co., Ltd. Matériau composite de résine et corps moulé

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017117054A1 (fr) 2015-12-30 2017-07-06 Braskem America, Inc. Composition polymère transparente et résistante aux chocs et article fabriqué
US10577159B2 (en) 2017-04-07 2020-03-03 Berry Plastics Corporation Drink cup lid
CN111182818B (zh) 2017-08-07 2023-07-04 贝瑞全球有限公司 用于热成型制品的方法和装置
CN110016097B (zh) * 2018-01-10 2021-12-31 中国石油化工股份有限公司 一种低溶出物、低熔点、窄分子量分布、热氧稳定的乙丙无规共聚物及其制备方法和应用
USD907997S1 (en) 2018-08-10 2021-01-19 Berry Global, Inc. Drink cup lid
EP3921154A4 (fr) 2019-02-06 2023-01-25 Berry Global, Inc. Procédé de formage d'un matériau polymère
US11891488B2 (en) 2019-02-06 2024-02-06 Berry Global, Inc. Polypropylene sheets and articles
USD911168S1 (en) 2019-03-05 2021-02-23 Berry Global, Inc. Drink cup lid
EP3940003A1 (fr) 2020-07-16 2022-01-19 Borealis AG Mélanges de polyoléfine translucides présentant un excellent niveau d'équilibre impact/rigidité et d'aptitude à l'écoulement
WO2023225346A1 (fr) * 2022-05-20 2023-11-23 W.R. Grace & Co.-Conn. Copolymère de polypropylène présentant une transparence et une ténacité élevées

Family Cites Families (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
IT1227893B (it) 1988-12-14 1991-05-14 Himont Inc Centerville Road Ne Composizioni polipropileniche aventi buona trasparenza e migliorata resistenza all'urto
EA199800481A1 (ru) 1995-11-24 1998-12-24 Чиссо Корпорейшн Композиции пропилена, способы их получения, композиции полипропилена, способы их получения и формованные изделия
US6635715B1 (en) 1997-08-12 2003-10-21 Sudhin Datta Thermoplastic polymer blends of isotactic polypropylene and alpha-olefin/propylene copolymers
EP1211289A1 (fr) 2000-11-29 2002-06-05 Borealis GmbH Composition de polyoléfines avec propriétés améliorées
EP1659151A1 (fr) 2004-11-18 2006-05-24 Borealis Technology OY Nouvelles compositions polymères de propylene
EP1669403A1 (fr) 2004-12-07 2006-06-14 Borealis Technology OY Nouveaux mélange de polymères de propylène
WO2006065649A1 (fr) 2004-12-17 2006-06-22 Exxonmobil Chemical Patents Inc. Melanges de polymeres heterogenes et articles moules realises avec ces melanges
ES2269021T5 (es) 2005-05-12 2012-06-27 Borealis Technology Oy Elemento laminar transparente y fácilmente rompible
EP1818365A1 (fr) 2006-02-14 2007-08-15 Borealis Technology Oy Compositions de polypropylène
DE602006019421D1 (de) 2006-08-17 2011-02-17 Borealis Tech Oy Verbesserte transparente Polypropylenzusammensetzung
EP1935938A1 (fr) 2006-12-18 2008-06-25 Borealis Technology Oy Appareil électronique
US8722833B2 (en) * 2006-12-22 2014-05-13 Basell Polyolefine Gmbh Multimodal polyethylene composition, mixed catalyst and process for preparing the composition
EP2022824A1 (fr) 2007-08-08 2009-02-11 Borealis Technology Oy Composition en polyprophylène stérilisable et à fort impact
JP5620998B2 (ja) 2009-11-25 2014-11-05 ダウ グローバル テクノロジーズ エルエルシー 低ヘイズおよび高透明性を有するポリマー成形品
EP2338656A1 (fr) 2009-12-23 2011-06-29 Borealis AG Polypropylène hétérophasique avec équilibre amélioré entre la raideur et la transparence
US8809461B2 (en) 2011-04-28 2014-08-19 Braskem America, Inc. Multimodal heterophasic copolymer and thermoformed articles from same
US8748539B2 (en) 2011-05-24 2014-06-10 Braskem America, Inc. Propylene impact copolymers having good optical properties
CN103998477B (zh) 2011-12-23 2016-11-09 博里利斯股份公司 用于注射成型制品或薄膜的丙烯共聚物
ES2552785T3 (es) 2011-12-23 2015-12-02 Borealis Ag Proceso para la preparación de un copolímero de propileno heterofásico
EP2746295A1 (fr) 2012-12-21 2014-06-25 Borealis AG Matériau d'emballage à paroi mince transparente avec une rigidité améliorée et une aptitude à l'écoulement
US10808111B2 (en) 2013-03-14 2020-10-20 Braskem America, Inc. Polypropylene impact copolymers with low haze
PL3102634T3 (pl) 2014-02-06 2020-11-16 Borealis Ag Miękkie i przezroczyste kopolimery odporne na uderzenia
PL3126411T3 (pl) 2014-04-04 2018-04-30 Borealis Ag Heterofazowy kopolimer propylenu o niskiej zawartości substancji ekstrahowalnych
ES2659731T3 (es) 2014-05-20 2018-03-19 Borealis Ag Composición de polipropileno para aplicaciones en interiores de automóviles
WO2017117054A1 (fr) 2015-12-30 2017-07-06 Braskem America, Inc. Composition polymère transparente et résistante aux chocs et article fabriqué
EP3246358A1 (fr) 2016-05-18 2017-11-22 Borealis AG Copolymères de propylène souple et transparent

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3926005A4 (fr) * 2019-02-12 2023-03-08 Furukawa Electric Co., Ltd. Matériau composite de résine et corps moulé

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